CN114134426B - Iron-based laser cladding layer powder and preparation method of iron-based laser cladding layer - Google Patents
Iron-based laser cladding layer powder and preparation method of iron-based laser cladding layer Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
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- C23C24/00—Coating starting from inorganic powder
- C23C24/08—Coating starting from inorganic powder by application of heat or pressure and heat
- C23C24/10—Coating starting from inorganic powder by application of heat or pressure and heat with intermediate formation of a liquid phase in the layer
- C23C24/103—Coating with metallic material, i.e. metals or metal alloys, optionally comprising hard particles, e.g. oxides, carbides or nitrides
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Abstract
The invention relates to the technical field of metal cladding layers, and particularly discloses iron-based laser cladding layer powder and a preparation method of an iron-based cladding layer. The iron-based laser cladding layer powder comprises the following chemical elements in percentage by mass: c:0.09% -0.1%, si:0.9% -1%, cr:15% -17%, ni:9% -10%, mo:8-14 percent, and the balance of Fe and inevitable impurities. The iron-based laser cladding layer powder provided by the invention forms a cladding layer on a substrate through a laser cladding method, has higher excellent wear resistance and corrosion resistance, forms a special crystal boundary and a substrate phase, completely eliminates a needle-shaped hard and brittle phase structure in an alloy cladding layer, greatly changes the structure, microhardness and wear resistance of the iron-based cladding layer, and achieves excellent comprehensive mechanical properties.
Description
Technical Field
The invention relates to the technical field of metal cladding layers, in particular to iron-based laser cladding layer powder and a preparation method of an iron-based cladding layer.
Background
In recent years, with the increase of the use frequency and the service life of army equipment parts, the probability of abrasion failure of transmission walking parts is higher and higher. Worn parts are mainly replaced at present, so that the problems of overhigh part replacement cost and serious resource waste are caused, and the war force guarantee of army equipment is seriously influenced.
In order to solve the above problems, laser cladding technology has been developed later. The technology can melt and cover iron-based alloy powder on the damaged part to form an alloy melting and covering layer with a certain function, so that the damaged part is repaired, the service life of the damaged part is prolonged, and the service life is prolonged. The repair technology not only saves cost and solves the problem of resource waste, but also can effectively ensure the fighting capacity of army walking pieces, and has important research value. However, although the hardness and the wear resistance of the surface of the component are improved to a certain extent by the existing iron-based alloy cladding layer, the wear resistance degree still cannot meet the higher actual use requirement, the bonding performance of the formed cladding layer and a matrix is poor, the crystal form in the cladding layer mainly consists of a needle-shaped structure and the matrix, the hardness and brittleness are high, the ductility is poor, and the conditions of cracks, cracking, peeling pits and deep furrows are easy to occur, so that the research on the coating layer which has good comprehensive mechanical property, high bonding strength with the matrix and good wear resistance, corrosion resistance and ductility has important significance for the army equipment components.
Disclosure of Invention
Aiming at the problems of the existing iron-based laser cladding layer, the invention provides iron-based laser cladding layer powder and a preparation method of the iron-based laser cladding layer.
In order to achieve the purpose of the invention, the embodiment of the invention adopts the following technical scheme:
an iron-based laser cladding layer powder comprises the following chemical elements in percentage by mass:
c:0.09% -0.1%, si:0.9% -1%, cr:15% -17%, ni:9% -10%, mo:8-14%, and the balance of Fe and inevitable impurities.
Compared with the prior art, the cladding layer formed on the substrate by combining the iron-based laser cladding layer powder and the laser cladding method changes the phase structure of the existing cladding layer, which mainly comprises an alpha-Fe matrix phase and acicular carbide Fe 7 C 3 (M 7 C 3 ) In the case of composition, a special grain boundary and a matrix phase are formed, and Fe is formed 7 C 3 (M 7 C 3 ) And Fe 7 Mo 3 The phase exists in a crystal boundary form, the grain size is between 3.5 and 6 mu m, the grains are uniformly refined, the phenomenon of Mo enrichment is shown in the crystal boundary, and the cladding is improved simultaneously by fine-grain strengthening and solid solution strengtheningHardness and ductility of the layer. The invention utilizes the iron-based laser cladding layer powder to form a cladding layer on a substrate through a laser cladding method, the cladding layer has high and excellent wear resistance, the wear resistance of the cladding layer is not in linear corresponding relation with microhardness, and the wear resistance is influenced by hardness and comprehensive factors such as grain size, strengthening phase quantity such as solid solution, type, size and distribution condition. The cladding layer completely eliminates needle-shaped hard and brittle phase structures in the alloy cladding layer, greatly changes the structure, microhardness and wear resistance of the iron-based cladding layer, and achieves excellent comprehensive mechanical properties.
Preferably, the iron-based laser cladding layer powder comprises the following chemical elements in percentage by mass:
c:0.09%, si:0.9%, cr:15.3%, ni:9%, mo:10%, and the balance of Fe and inevitable impurities.
The selected elemental composition of the iron-based laser cladding powder can further improve the wear resistance, corrosion resistance and ductility of the resulting cladding layer.
Preferably, the particle size of the iron-based laser cladding layer powder is 50 μm to 100 μm.
The average particle size of the preferred iron-based laser cladding powder is selected to further increase the structural uniformity of the resulting cladding layer.
The invention also provides a preparation method of the iron-based cladding layer, which comprises the following steps: and forming the iron-based laser cladding layer on an iron matrix by adopting the iron-based laser cladding layer powder through a laser cladding method.
Preferably, the preparation method of the iron-based cladding layer comprises the following steps: and drying the iron-based laser cladding layer powder, adding the dried iron-based laser cladding layer powder into a powder feeder of a fiber laser, and simultaneously carrying out powder feeding and laser scanning on the iron substrate to form the iron-based cladding layer on the iron substrate.
Preferably, the drying temperature is 50-100 ℃ and the drying time is 1-2 h.
Preferably, the powder feeding mode of the powder feeder is an argon paraxial powder feeding mode.
Preferably, the powder feeding speed of the powder feeder is 10g/min-15g/min.
Preferably, the power of the laser scanning is 225W-250W, and the speed is 2.5mm/s-3.5mm/s.
The above preferred parameter setting of laser scanning, in combination with the specific powder feeding rate, can further ensure the thickness uniformity and the structure uniformity of the cladding layer, ensure the uniformity of the mechanical strength of the cladding layer, and can further refine the crystal grains and promote the formation of the crystal boundary.
The invention also provides the iron-based cladding layer prepared by the preparation method of the iron-based cladding layer.
Drawings
Fig. 1 is a schematic structural diagram of a fiber laser system in embodiment 1 of the present invention, in which 1, a constant current fiber laser, 2, a powder feeder, 3, a reflector, 4, a lens, 5, and an iron substrate;
FIG. 2 is a metallographic structure chart of a cladding layer examined in test example 1 of the present invention;
FIG. 3 is an X-ray diffraction analysis chart of a cladding layer detected in test example 1 of the present invention;
FIG. 4 is a hardness indentation morphology image obtained by microhardness detection of the cladding layer in test example 1 of the present invention;
FIG. 5 is a graph showing the wear-out profile of the cladding layer measured in test example 1 of the present invention.
Detailed Description
In order to make the objects, technical solutions and advantages of the present invention more apparent, the present invention is further described in detail with reference to the following embodiments. It should be understood that the specific embodiments described herein are merely illustrative of the invention and are not intended to limit the invention.
Example 1
An iron-based laser cladding layer powder comprises the following chemical elements in percentage by mass:
c:0.09%, si:1%, cr:17%, ni:10%, mo:8 percent, and the balance of Fe and inevitable impurities, and the particle size of the iron-based laser cladding layer powder is 50-100 mu m.
The method for preparing the iron-based cladding layer by adopting the iron-based laser cladding layer powder comprises the following steps:
drying iron-based laser cladding layer powder at 100 ℃ for 1h, adding the powder into a powder feeder of an optical fiber laser system, and then carrying out laser scanning on an iron matrix (a loading wheel, 40Cr steel) while feeding the powder by the powder feeder to form an iron-based cladding layer on the iron matrix. The powder feeding mode is an argon paraxial powder feeding mode, the powder feeding speed is 15g/min, the power of laser scanning is 250W, and the speed is 3.5mm/s.
The schematic structural diagram of the fiber laser system is shown in fig. 1, and comprises a constant current fiber laser 1, a reflector 3, a lens 4 and a powder feeder 2. The laser beam emitted by the constant current fiber laser 1 is reflected by the reflector 3 and then reaches the iron matrix 5 through the lens 4, and meanwhile, the powder feeder 2 feeds the iron-based laser cladding layer powder to the laser scanning position on the iron matrix 5 in an argon paraxial powder feeding mode to prepare the iron-based cladding layer.
Example 2
An iron-based laser cladding layer powder comprises the following chemical elements in percentage by mass:
c:0.1%, si:0.95%, cr:16%, ni:9.5%, mo:14%, and the balance Fe and inevitable impurities, wherein the particle size of the iron-based laser cladding layer powder is 50-100 μm.
The method for preparing the iron-based cladding layer by adopting the iron-based laser cladding layer powder comprises the following steps:
drying iron-based laser cladding layer powder at 50 ℃ for 2h, adding the dried powder into a powder feeder of a fiber laser system, and then carrying out laser scanning on an iron matrix (a loading wheel, 40Cr steel) while feeding the powder by the powder feeder to form the iron-based cladding layer on the iron matrix. The powder feeding mode is an argon paraxial powder feeding mode, the powder feeding speed is 10g/min, the laser scanning power is 225W, and the speed is 2.5mm/s.
Example 3
An iron-based laser cladding layer powder comprises the following chemical elements in percentage by mass:
c:0.09%, si:0.9%, cr:15.3%, ni:9%, mo:10% and the balance Fe and unavoidable impurities, the particle size of the iron-based laser cladding layer powder being 50-100 μm.
The method for preparing the iron-based cladding layer by adopting the iron-based laser cladding layer powder comprises the following steps:
drying iron-based laser cladding layer powder at 80 ℃ for 1.5h, adding the dried powder into a powder feeder of a fiber laser system, and then carrying out laser scanning on an iron matrix (bogie wheel, 40Cr steel) while feeding the powder by the powder feeder to form the iron-based cladding layer on the iron matrix. The powder feeding mode is an argon paraxial powder feeding mode, the powder feeding speed is 12.5g/min, the laser scanning power is 250W, and the speed is 3mm/s.
Test example 1
The iron-based cladding layers obtained in examples 1 to 3 were analyzed for microstructure, phase structure, microhardness, and frictional wear properties:
the analysis method comprises the following steps:
cutting the prepared cladding layer by using a wire cutting machine, grinding and polishing by using sand paper, mixing a nitric acid solution with the concentration of 42.24wt% and hydrochloric acid with the concentration of 36wt% (the mixed volume ratio is 1:3) to be used as a corrosive, wherein the corrosion time is about 10s, observing and analyzing the microstructure of the sample section by using a German Zeiss metallographic microscope and a TESCAN VEGA tungsten filament scanning electron microscope, and analyzing the components of a micro-area by using an energy spectrum analyzer;
carrying out phase structure analysis on the cladding layer by using a Japan science SmartLab9KW type X-ray diffractometer;
testing the hardness of the surface layer of the cladding layer to the longitudinal section of the substrate by using a TMVS-1 type Vickers microhardness tester, testing once every 100 micrometers, averaging the 3-time measurement results, wherein the load is 200g, and the loading time is 10s;
the friction and wear performance test of the matrix and the cladding layer is carried out in a wear testing machine, ultrasonic cleaning and weighing are carried out before and after wear, a mode of forward rotation and opposite grinding of an upper grinding disc and a lower grinding disc is adopted, the upper grinding disc is used for fixing a sample, a friction pair of the lower grinding disc is 320# coarse abrasive paper, normal force is applied in the wear test at 30N, the rotating speed of the grinding disc is 80r/min, the wear time is 10min, the mass of the sample before and after wear is weighed by a thousandth of precision balance, and the average weight loss and the relative wear resistance (weight loss in unit area) are calculated;
and evaluating the appearance of the wear surface by using a scanning electron microscope.
And (3) analysis results:
the structural morphology of the iron-based cladding layer in example 1 is shown in fig. 2, where fig. 2a is a metallographic structure photograph (OM) of the obtained cladding layer, fig. 2b, 2c, and 2d are high-power metallographic microstructure morphologies of the three positions from the surface layer to the transition interface in fig. 2a, respectively, and the thickness of the cladding layer is about 800 μm. As can be seen from FIG. 2, the internal transition layer structure mainly comprises dendrites extending from the interface to the middle upper portion, gradually transitions to form a columnar crystal structure at the middle portion, and the near-surface layer structure is transformed and grown from the columnar crystal structure to an equiaxial crystal or cell crystal structure. Since laser cladding is a rapid melting and cooling process, the microstructure of the cladding layer is mainly determined by the temperature gradient (G) and the solidification rate (R) in the rapid solidification process, namely the ratio of G/R. At the bottom of the coating, the temperature difference of a solid-liquid interface is large, namely, the temperature gradient takes the leading action, at the moment, the value of G/R is large, and the undercooling is almost not existed, so that the dendritic crystal growth is realized in the bottom region; along with the increase of the distance between the cladding layer and the fusion zone, the temperature gradient is gradually reduced compared with that of the bottom zone, and the undercooling of the components hinders the growth of dendrites, so that the cladding layer is mainly of a columnar crystal structure in the middle; along with the reduction of the temperature gradient, G/R is gradually reduced, the undercooling plays a leading role, and in the region from the middle part to the top part, the cladding layer is converted from columnar crystal to isometric crystal, so that the solidification theory growth rule of the tissue is met. Meanwhile, the structural morphology of the cladding layers obtained in example 2 and example 3 is substantially equivalent to that of example 1.
The line scanning is carried out on the boundary of the fusion area of the iron-based cladding layer and the substrate in the embodiment 1, and the scanning result shows that the Fe element is gradually increased from the cladding layer to the substrate by taking a fusion line as the boundary, and the Mo element, the Cr element and the Ni element are gradually reduced, which indicates that in the laser cladding process, the metal alloy powder and the substrate form a molten pool, and part of the Fe element is diffused into the cladding layer from the substrate; meanwhile, mo, cr and Ni elements in the cladding layer part are decomposed and diffused into the matrix, and the cladding layer and the matrix form good metallurgical bonding, so that the interface stress in an interface fusion area is relieved. The line scanning results of the boundary between the cladding layer and the substrate obtained in examples 2 and 3 showed the same changes in the distribution of the elements as in example 1.
X-ray diffraction (XRD) analysis of the iron-based cladding layer in example 3 showed that as shown in fig. 3, it can be seen from fig. 3 that the phase of the iron-based cladding layer is significantly changed from that of the conventional cladding layer, another α -Fe peak appears near the main peak, and Fe appears in the cladding layer 7 Mo 3 Phase and Fe 7 C 3 The (M7C 3) carbide and the alpha-Fe phase are reduced. The same analysis was performed for the cladding layers of examples 1 and 2, in which Fe was also present in the cladding layer 7 Mo 3 And (4) phase(s).
The grain size of the cladding layers in the embodiments 1-3 is measured by combining a metallographic structure diagram with Image Pro-plus software, the average grain size of the cladding layer in the embodiment 1 is 6.0 mu m, the structure characteristics are obvious, the cladding layer exists in the forms of grain boundaries and matrix phases, the grains are refined to play a strengthening role, and Mo element is easily dissolved in the grain boundaries to increase the ductility of the cladding layer. The grain refinement degree of the phase structure of the cross section of the iron-based cladding layers of the embodiment 2 and the embodiment 3 is higher, the average grain size of the cladding layer in the embodiment 2 is 4.8 μm, the average grain size of the cladding layer in the embodiment 3 is 3.5 μm, and the structure characteristics in the embodiment 2 and the embodiment 3 are more obvious compared with the embodiment 1.
When the phase structure surface scanning element distribution of the cladding layer in example 1 is analyzed, different element distribution rules are different, and the cladding layer can be transformed in different forms (such as solid solution and compound) during the solidification process mainly due to different chemical binding forces among the alloy elements. Wherein, ni and Cr are relatively uniformly distributed in the cladding layer, but Fe is more distributed in the matrix phase; in addition, mo and C elements are mainly enriched at grain boundaries, and the phenomenon that Mo and C are enriched at the grain boundaries is mainly a combined phase of metal compounds and carbides of Fe and Mo. The phase structure surface scanning element distribution pattern of the cladding layers in example 2 and example 3 is substantially the same as that in example 1.
The micro-hardness detection indentation morphology of the cladding layer in example 1 is shown in fig. 4, and it can be seen from the figure that the difference in the sizes of the hardness indentation morphologies from the upper part to the lower part of the coating layer is not large, which indicates that the overall hardness distribution of the coating layer is relatively uniform, and no cracks or defects are found near the hardness indentation, so that the coating layer has good ductility and ductility. The hardness of the cladding layers of examples 2 to 3 tested in the same manner was uniform, and no cracks or defects were observed in the vicinity of the indentation.
The wear performance of the cladding layer in example 1 is tested, the wear is an important experimental method for the wear resistance of the material to be tested, and the plane fixation grinding is still the main wear mode. The test adopts the abrasive wear form to evaluate the wear performance of the surface to be measured. Analyzing the wear resistance by the wear weight loss of the iron-based cladding layer and the bogie wheel matrix in unit area, wherein the relative wear-resisting multiplying power relation expression of the iron-based cladding layer and the bogie wheel matrix is as follows: beta = weight loss of friction wear of the base body of the bogie wheel/weight loss of friction wear of the cladding layer. After the bogie wheel matrix and the iron-based cladding layer are worn, the cumulative weight loss per unit area is 236mg and 122mg respectively, and the relative wear resistance multiplying power of the cladding layer is 1.93 times of that of the bogie wheel matrix. The abrasion weight loss of the iron matrix is large, and the abrasion resistance of the cladding layer is obviously improved. The presence of carbide hard phases and intermetallic compounds in the cladding layer is an important reason for increasing its relative wear resistance. In combination with microhardness, the wear resistance of the cladding layer is not in linear correspondence with the hardness thereof, and is different from the wear resistance law of common cladding layer materials. While the relative wear resistance rates of the cladding layers in examples 2-3 were 2.01 and 1.96 times that of the bogie base body, respectively
The appearance graphs of the worn iron-based cladding layers in the examples 1 and 3 are shown in fig. 5, and it can be seen from the macroscopic appearance combined with the wear weight loss that after the iron-based cladding layers are worn for 10min under the action of 30N load, the wear resistance of the load wheel matrix is the worst, the appearance characteristics are represented by more peeling pits and deeper furrows, the main wear mechanism is wear of abrasive particles, and meanwhile, partial plastic deformation exists, as shown in fig. 5 a; the scratch depth of the cladding layer in example 1 becomes remarkably shallow, and the flatness of the abraded surface is more uniform. As shown in fig. 5 b; the wear scar on the clad layer surface in example 3 was further reduced, and peeling and cracking were hardly caused, and as shown in fig. 5c, the wear resistance was excellent. While the wear resistance of the cladding layer in example 2 is between that of the cladding layers of examples 1 and 3.
In view of the above-mentioned properties, the type and content of the phase in the cladding layer of the present invention are changed, the acicular carbide phase disappears, and M in the form of grain boundaries appears 7 C 3 Carbide and Fe 7 Mo 3 The metal compound has more uniform and refined structure, good bonding property of the reinforcing phase and the matrix phase, uniform load and wear resistance in the aspect of wear resistance, good ductility and no crack and cracking phenomenon.
The above description is only for the purpose of illustrating the preferred embodiments of the present invention and is not to be construed as limiting the invention, and any modifications, equivalents or improvements made within the spirit and principle of the present invention should be included in the scope of the present invention.
Claims (5)
1. A preparation method of an iron-based cladding layer is characterized by comprising the following steps: the method comprises the following steps: drying iron-based laser cladding layer powder, adding the dried iron-based laser cladding layer powder into a powder feeder of a fiber laser, and then simultaneously carrying out powder feeding and laser scanning on an iron substrate by the powder feeder to form the iron-based cladding layer on the iron substrate;
the powder feeding mode of the powder feeder is an argon paraxial powder feeding mode;
the powder feeding speed of the powder feeder is 10-15 g/min;
the power of the laser scanning is 225W-250W, and the speed is 2.5mm/s-3.5mm/s;
the iron-based laser cladding layer powder comprises the following chemical elements in percentage by mass:
c:0.09% -0.1%, si:0.9% -1%, cr:15% -17%, ni:9% -10%, mo:8-14 percent, and the balance of Fe and inevitable impurities.
2. The method of producing an iron-based cladding layer according to claim 1, wherein: the iron-based laser cladding layer powder comprises the following chemical elements in percentage by mass:
c:0.09%, si:0.9%, cr:15.3%, ni:9%, mo:10%, and the balance of Fe and inevitable impurities.
3. The method of producing an iron-based cladding layer according to claim 1, wherein: the particle size of the iron-based laser cladding layer powder is 50-100 mu m.
4. The method of producing an iron-based cladding layer according to claim 1, wherein: the drying temperature is 50-100 ℃, and the drying time is 1-2 h.
5. An iron-based cladding layer produced by the method for producing an iron-based cladding layer according to any one of claims 1 to 4.
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